Low carbon microalloyed steel

ABSTRACT

A low carbon microalloyed steel, comprising in weight % about: 0.05-0.30 C; 0.5-1.5 Mn; 0.04 max S; 0.025 max P; 1.0 max Si; 0.5-2.0 Ni; 0.05-0.30 V; 0-2.0 Cu; up to 0.0250 N; up to 0.2 Cb; up to 0.3 Cr; up to about 0.15 Mo; up to about 0.05 Al; balance Fe and minor additions and impurities. The steel has a carbon equivalent value, C.E., ranging between 0.3-0.65, calculated by the formula: C.E.=C+Mn+Si+Cu+Ni+Cr+Mo+V+Cb 6 15 5

BACKGROUND OF THE INVENTION

The present invention relates generally to the metallurgy of steel and, more particularly, to low carbon microalloyed steel compositions. It is common practice to use conventional microalloyed steels in various applications for bars and tubular products. However, there are needs for stronger and tougher microalloyed steels in a number of different applications such as, for example, in communication towers and hub assemblies.

SUMMARY OF THE INVENTION

The steels of the present invention are much more weldable and tougher than conventional microalloyed steels. The present invention is directed to an alloy broadly comprising in wt. %, about 0.05-0.30 C; up to 1.5 Mn; 1.0 max Si; 0.5-2 Ni; 0.05-0.3 V; up to 2 Cu; 10-250 ppm N; balance Fe and other minor additions and impurities.

BRIEF DESCRIPTION OF THE DRAWING

FIG. 1 is a graph schematically showing the relationship between the precipitation strengthening factor (ΔYS_(p)) and the Ar₃ temperature in the steels of the present invention.

DETAILED DESCRIPTION OF THE INVENTION

The family of microalloyed steels of the present invention provide better weldability and much higher impact toughness and tensile ductility than conventional microalloyed steels. A critical factor in the design of microalloyed ferrite pearlite steels is the extent to which precipitation strengthening supplements the base strength provided by solid solution and grain refinement. It is known that this precipitation strengthening factor, referred to as ΔYS_(p), is controlled by the ferrite transformation temperature, Ar₃, all other things being equal. As the Ar₃ temperature is lowered, ΔYS_(p) increases up to a maximum and then decreases as a result of precipitation suppression through the usual kinetic limitations at lower temperatures. This relationship is graphically depicted in FIG. 1. The essential design factor for high strength involving precipitation is to adjust Ar₃ by compositional means to allow this maximum to be obtained. Either under (lean) or over (rich) adjustment of the chemistry of the alloy may lead to underutilization of precipitation. Accordingly, two factors must be considered in order to optimize the precipitation according to the invention. The first factor is whether the base composition is too close to the critical limit for formation of bainite such that any further increase in either Mn or Ni (both lower the Ar₃ temperature) causes unwanted bainite formation. The second factor is that for a given Ar₃ temperature, Mn is less potent than Ni in that it suppresses precipitation. Thus, the invention requires the Mn levels to be below 1.5 wt. % and that the Ar₃ temperature be controlled with elements which have a low tendency for forming bainite.

Consideration of these requirements shows that out of all the common alloying elements, Ni is the most effective. The results of a study to examine the effect of Ni on ΔYS_(p) showed that 45 ksi minimum yield strength and as high as 80 ksi was possible for large bars or tubular products. The results are given in the following tables.

One presently preferred alloy composition according to the present invention contains in % by weight: 0.05-0.30 C, 0.5-1.5 Mn; 1.0 max Si; 0.5-2.0 Ni; 0.05-0.30 V; 0-2.0 Cu; 0.0050-0.0250 N; balance Fe and other minor additions and impurities. The S level is 0.04 wt. % max and preferably about 0.035 wt. % max. The P content is 0.025 wt. % max and preferably about 0.02 wt. % max. In the above composition, the C and N contents may preferably be 0.05-0.15 wt. % C and 0.0010-0.0250 wt. % N.

A further presently preferred embodiment of the present invention includes the alloy composition set forth above, also containing about 0.25-2.0 wt. % Cu. Copper in these microalloyed steels will form as E-copper particles by both interphase precipitation and the normal nucleation and growth process, thus increasing strength by increasing ΔYS_(p), and maintaining high levels of toughness and tensile ductility as seen in Tables III and IV.

The alloy may also contain additional constituents such as Cr, Mo, Cb and Al, for example, 0.05-0.3 Cr, up to about 0.15 Mo, up to about 0.2 Cb, up to about 0.05 Al, and more preferably about 0.01-0.03 Al. TABLE I Chemical Compositions Heat No. C Mn P S Si Cr Ni Mo Cu Al V N(ppm) C.E.* 2032 0.08 0.52 0.005 0.004 0.25 0.12 1.03 0.03 0.01 0.022 0.144 103 0.34 2033 0.14 0.53 0.004 0.004 0.26 0.12 1.03 0.03 0.01 0.026 0.146 106 0.40 2034 0.07 0.52 0.004 0.004 0.27 0.11 1.03 0.03 0.01 0.026 0.152 20 0.33 2035 0.13 0.52 0.004 0.004 0.26 0.11 1.05 0.03 0.01 0.026 0.138 20 0.39 2036 0.07 0.98 0.005 0.004 0.25 0.11 1.04 0.03 0.01 0.021 0.143 107 0.40 2037 0.14 1.02 0.005 0.004 0.26 0.12 1.03 0.03 0.01 0.024 0.140 112 0.48 2057 0.06 1.03 0.004 0.005 0.26 0.12 1.03 0.03 0.01 0.025 0.146 174 0.40 2058 0.11 1.04 0.004 0.005 0.28 0.12 1.04 0.04 0.01 0.017 0.150 164 0.46 2059 0.08 1.06 0.004 0.005 0.26 0.12 1.54 0.03 0.01 0.023 0.131 186 0.46 2060 0.13 1.03 0.004 0.005 0.25 0.12 1.52 0.03 0.01 0.023 0.148 187 0.51 2061 0.07 1.03 0.004 0.005 0.27 0.12 1.04 0.03 0.01 0.024 0.249 184 0.44 2062 0.12 1.03 0.004 0.005 0.26 0.12 1.03 0.03 0.01 0.029 0.250 176 0.48 2063 0.08 1.02 0.004 0.006 0.26 0.12 1.03 0.03 0.50 0.025 0.152 180 0.46 2135 0.16 1.04 0.004 0.004 0.26 0.14 1.5 0.03 0.01 0.028 0.138 166 0.54 2136 0.26 1.00 0.003 0.004 0.26 0.13 1.5 0.03 0.01 0.028 0.137 170 0.63 2137 0.19 1.00 0.004 0.004 0.26 0.14 0.98 0.03 0.01 0.025 0.227 168 0.55 2138 0.28 1.00 0.004 0.003 0.26 0.14 0.96 0.03 0.01 0.028 0.218 156 0.63 ${*{C.E.}} = {C + \frac{{Mn} + {Si}}{6} + \frac{{Cu} + {Ni}}{15} + \frac{{Cr} + {Mo} + V + {Cb}}{5}}$

TABLE II Rolling Schedule (1) All billets had a 2250° F. soak (2) Rolling Sequence: Pass No. Reduction (Inches) 1 2.625-2.000 2 2.000-1.750 3 1.750-1.500 4 1.500-1.250 5  1.25-1.000 6 Cross Roll to Straighten Plate (No reduction) (3) Finish Rolling Temperature (approximately 1950° F. to 2000° F.) (4) No designation after heat number: Air cooled “S” designation after heat number: Sand cooled to simulate the mid-radius position of a 6-inch bar

TABLE III Tensile Properties and Hardness Ultimate Yield Strength Tensile Elongation R.A. Hardness Heat No. (0.2% offset) (ksi) Strength (ksi) (Percent in 1.4″) (Percent) (R_(B)) 2032 54.6 70.3 32.0 77.1 81 2032 S 47.7 64.6 32.7 74.7 74 2033 61.3 80.8 28.9 70.6 87 2033 S 51.4 73.1 28.6 67.4 81 2034 50.2 68.3 31.1 76.9 80 2034 S 46.4 65.2 33.1 77.5 74 2035 56.4 79.2 27.8 71.1 86 2035 S 48.2 70.3 30.4 69.7 79 2036 61.9 79.7 28.2 77.1 87 2036 S 52.2 74.3 28.9 77.2 82 2037 70.3 90.8 28.4 72.1 92 2037 S 62.3 83.6 29.9 70.6 88 2057 64.8 84.9 28.0 75.8 91 2057 S 56.8 76.0 30.5 74.4 85 2058 68.3 87.4 28.4 74.2 92 2058 S 60.1 80.6 28.4 73.7 87 2059 71.0 95.1 26.1 72.9 95 2059 S 66.4 87.0 27.8 74.0 92 2060 75.6 101.6 24.4 68.3 98 2060 S 70.3 95.6 24.1 67.2 95 2061 69.8 90.6 26.2 75.3 94 2061 S 60.8 79.6 27.1 75.6 88 2062 74.8 100.2 23.8 65.5 97 2062 S 67.4 90.4 24.2 65.7 94 2063 70.8 90.8 26.6 71.8 93 2063 S 65.5 84.8 28.1 72.6 90 2135 80.3 109.7 23.5 67.9 98 2135 S 72.7 100.2 25.1 67.3 94 2136 89.2 129.2 20.3 53.7 103 2136 S 82.6 116.4 21.2 55.8 99 2137 89.2 118.3 21 54.7 100 2137 S 74.3 103.5 22.6 57.3 96 2138 103 136.7 15.9 39.5 104 2138 S 82.7 117.8 17.9 47.6 100

TABLE IV Impact Toughness Charpy V-notch Impact Toughness (ft-lbs) Test Temperature Heat No. +40° F. 0° F. −20° F. −60° F. 2031 264.0 106.0 9.5 5.0 — 13.0 11.0 — 2032 S — 262.0 20.0 8.0 — 260.0 113.0 7.5 2033  79.5 10.5 10.5 —  15.5 25.5 5.0 — 2033 S  81.0 26.5 9.0 — 102.0 51.5 11.0 — 2034 270.0 7.0 6.5 3.0 — — 5.5 — 2034 S 266.0 12.5 6.0 3.5 — 8.0 9.0 — 2035  14.5 9.0 8.0 —  9.0 12.0 3.5 — 2035 S  10.0 9.0 5.5 —  31.0 8.5 6.0 — 2036  97.5 7.0 10.0 — 222.0 112.0 6.0 — 2036 S — 280.0 160.0 4.0 — — 8.0 9.5 2037  68.5 57.5 44.0 —  92.5 37.0 56.5 — 2037 S 110.0 81.5 91.5 — 121.0 90.0 70.0 — 2057  84.5 107.5 7.5 5.0 — 108.0 53.0 23.0 2057 S 219.0 153.0 124.0 2.5 — — 77.5 53.0 2058 112.0 84.5 53.5 9.5 — 57.0 43.0 16.0 2058 S 144.0 95.0 104.0 41.5 — 102.5 75.5 6.0 2059  59.0 6.5 26.5 4.0 — — 41.0 3.0 2059 S 107.0 88.5 49.5 9.5 — 81.0 51.5 7.0 2060  32.5 8.5 6.0 2.0 — 29.5 6.0 4.5 2061  45.5 24.5 24.5 5.0 — 14.5 6.0 8.0 2061 S 125.0 103.5 60.0 6.0 — 92.0 19.0 8.5 2062  11.0 11.0 12.0 3.5 — 25.0 10.5 3.5 2062 S  26.0 7.5 2.5 3.0 — 37.0 5.0 11.5 2063  63.0 16.5 18.0 22.5 — 17.5 16.0 7.5 2063 S 127.0 115.0 74.5 57.5 — 76.5 52.5 7.5 Heat No. +250° F. +205° F. +150° F. +68° F. +32° F. 2135 — 75.5 48.5 24.5 19.0 — — 66.0 18.5 7.0 — — — 30.5 — 2135 S — 94.5 74.5 51.5 52.5 — — 83.0 43.0 34.0 — — — 60.0 — 2136  48.0 28.0 24.0 12.5 — — 21.5 20.0 8.0 — — — — 15.0 — 2136 S  57.0 37.5 27.5 20.0 — — 39.0 24.5 20.5 — — — — 18.5 — 2137  49.5 28.5 25.5 6.0 — — 31.5 18.0 10.0 — — — — 13.5 — 2137 S  49.5 55.5 37.0 26.0 — — 36.0 42.5 11.5 — — — — 19.0 — 2138  20.5 18.5 12.0 7.0 —  23.0 13.5 14.0 10.0 —  20.0 — — 8.0 — 2138 S  36.5 24.5 20.5 5.0 —  31.5 24.0 21.0 9.5 — — — — 8.0 —

The “C.E.” or carbon equivalent values reported in Table I may broadly range between 0.3 and 0.65 but, more preferably, are controlled within a range of 0.3 to 0.55 and, still more preferably, controlled within a range of 0.4-0.5 to ensure superior physical properties. The C.E. value of an alloy is calculated using the following formula: ${C.E.} = {C + \frac{{Mn}\quad + {Si}}{6} + \frac{{Cu} + {Ni}}{15\quad} + \frac{{Cr} + {Mo} + V + {Cb}}{5}}$ Various alloy compositions of the present invention are set forth in Table I which also includes the calculated C.E. values for each. Table II describes the rolling schedule for each of the steel alloy heats made from the compositions of Table I. It will be noted that the billets were either air cooled after completion of rolling or they were sand cooled to simulate the mid-radius position of a large diameter bar of, for example, a 6-inch diameter bar. These sand cooled rolled heats have an “S” designation in Tables III and IV while the rolled heats that, were air cooled have no letter designation in the tables.

While specific embodiments of the invention have been described in detail, it will be appreciated by those skilled in the art that various modifications and alternatives to those details could be developed in light of the overall teachings of the disclosure. The presently preferred embodiments described herein are meant to be illustrative only and not limiting as to the scope of the invention which is to be given the full breadth of the appended claims and any and all equivalents thereof. 

1. A low carbon microalloyed steel, comprising in weight % about: 0.05-0.30 C, 0.5 to less than 1.5 Mn; 0.04 max S; 0.025 max P; 1.0 max Si; 0.5-2.0 Ni; 0.05-0.30 V; 0.01-2.0 Cu; up to 0.0250 N; up to 0.2 Cb; 0.05-0.3 Cr; up to 0.15 Mo; up to 0.05 Al; balance Fe and minor additions and impurities.
 2. The steel of claim 1 containing 0.25-2.0 Cu.
 3. The steel of claim 1 containing 0.05-0.15 C.
 4. The steel of claim 1 containing 0.0010-0.0250 N.
 5. The steel composition of claim 1 containing 0.01-0.03 Al.
 6. The steel of claim 1 in the form of a bar or tubular shape having a minimum yield strength of 45-80 ksi.
 7. The steel of claim 7 haying a minimum yield strength of 65 ksi.
 8. The steel of claim 1 having a carbon equivalent value, C.E., ranging between 0.3-0.65, calculated by the formula: ${C.E.} = {C + \frac{{Mn}\quad + {Si}}{6} + \frac{{Cu} + {Ni}}{15\quad} + \frac{{Cr} + {Mo} + V + {Cb}}{5}}$
 9. A low carbon microalloyed steel having a minimum yield strength of between 45-80 ksi, comprising in weight %: 0.05-0.30 C, 0.5-1.5 Mn; 1.0 max Si; 0.04 max S; 0.025 max P; 0.5-20 Ni; 0.05-0.3 V; 0.01-2.0 Cu; 10-250 ppm N; up to 0.2 Cb; 0.05-0.3 Cr: up to 0.15 Mo; up to 0.05 Al; balance Fe and incidental additions and impurities; and wherein said steel has a carbon equivalent value, C.E., of between about 0.3-0.65, derived from the following formula: ${C.E.} = {C + \frac{{Mn}\quad + {Si}}{6} + \frac{{Cu} + {Ni}}{15\quad} + \frac{{Cr} + {Mo} + V + {Cb}}{5}}$
 10. The steel of claim 10 wherein the C.E. value is between 0.4-0.5. 